Luminescent metal halide perovskites and methods

ABSTRACT

Nanoscale metal halide perovskites are provided. The nanoscale metal halide perovskites may have a 2D structure, a quasi-2D structure, or a 3D structure. Methods also are provided for making the nanoscale metal halide perovskites. The color emitted by the nanoscale metal halide perovskites may be tuned.

CROSS-REFERENCE TO RELATED APPLICATIONS

This application is a divisional application of U.S. patent applicationSer. No. 15/869,304, filed Jan. 12, 2018, which is a divisional of U.S.patent application Ser. No. 15/354,558, filed Nov. 17, 2016, now U.S.Pat. No. 9,908,906, issued Mar. 6, 2018, which claims priority to U.S.Provisional Patent Application No. 62/267,342, filed Dec. 15, 2015. Thecontent of these applications is incorporated herein by reference.

BACKGROUND

Earth abundant organometal halide perovskites have emerged as apromising class of light emitting materials that may exhibit high colorpurity and tunability. While bulk perovskite thin films can be preparedby relatively facile low temperature solution processing, they oftensuffer from low photoluminescence quantum efficiency (PLQE), possiblydue to emission quenching caused by defects. Although single crystallinenano/microscale perovskites have demonstrated high PLQEs, they have beenprepared only by wet-chemistry methods. For example, green emittingnanoscale three-dimensional (3D) methylammonium lead bromide perovskites(MAPbBr₃) prepared by wet-chemistry techniques have shown PLQEs up to93%. (see, e.g., L. C. Schmidt et al. J. Am. Chem. Soc., 2014, 136,850-853; S. Gonzalez-Carrero et al. J. Mater. Chem. A, 2015, 3,9187-9193; H. Huang et al. Advanced Science, 2015, 2, 1500194; C. Muthuet al. Rsc. Adv., 2014, 4, 55908-55911; and O. Vybornyi et al.Nanoscale, 2016, DOI: 10.1039/c5nr06890h).

Highly luminescent two-dimensional (2D) layered lead bromide perovskitenano/microdisks with deep blue emissions also have been reported (S.Gonzalez-Carrero et al. J. Mater. Chem. A, 2015, 3, 14039-14045; P.Audebert et al. Chem. Mater., 2009, 21, 210-214; L. T. Dou et al.Science, 2015, 349, 1518-1521). In addition to higher PLQEs, thesenanoscale perovskites also have shown purer and narrower emissions, andhigher stability, as compared to their bulk counterparts. The methodsused to synthesize these perovskites and others, however, typically aredifficult, suffer from relatively low product yields, and/or do notproduce high quality perovskites either consistently or at all.

Organometal halide perovskites also have been demonstrated to exhibithigh color tunability across the visible to near infrared regions. Thisfeature has been explored through synthetic control of 3D perovskitestructures by using different halide anions, i.e., Cl, Br, I, and theirmixtures (see, e.g., F. Zhang et al. Acs. Nano., 2015, 9, 4533-4542; D.M. Jang et al. Nano. Lett., 2015, 15, 5191-5199; N. Pellet et al. Chem.Mater., 2015, 27, 2181-2188; Y. H. Kim et al. Adv. Mater. 2015, 27,1248-1254; and J. H. Noh et al. Nano. Lett. 2013, 13, 1764-1769).

The use of bulk quasi-2D layered lead(II) iodide perovskites withtunable absorptions as light absorber in photovoltaic cells (PVs) hasbeen reported (I. C. Smith et al. Angew. Chem. Int. Edit., 2014, 53,11232-11235; and D. H. Cao et al. J. Am. Chem. Soc., 2015, 137,7843-7850). Although these hybrid perovskites have shown better moistureresistance than pure 3D perovskites, the color tuning of perovskites byorganic cations remains challenging, due at least in part to thewet-chemistry techniques used to prepare them. This likely is due, atleast in part, to the difficulty associated with controlling crystalgrowth in a solution phase containing different organic cations. Due atleast in part to this difficulty, non-uniform products with impureemissions often are produced.

Also, the color tuning of lead (II) bromide perovskites by using organiccations to control the thickness of the obtained nanoplatelets has beenreported, but the products suffer from relatively low quantumefficiency, and their emissions are not pure, i.e., include broad andmultiple peaks, due at least to the fact that the process results in theformation of mixed perovskites having different thicknesses (J. A.Sichert et al. Nano. Lett., 2015, 15, 6521-6527).

Therefore, there remains a need for nanoscale metal halide perovskitesthat are stable, color tunable, exhibit narrow emissions, have highquantum efficiencies, and/or are capable of being made by a relativelysimple process that may permit control over the crystalline structure ofthe nanoscale metal halide perovskites.

BRIEF SUMMARY

Provided herein are nanoscale metal halide perovskites. In embodiments,the nanoscale metal halide perovskites comprise a crystal having a unitcell according to formula (I) or (II):(RNH₃)(R′NH₃)(CH₃NH₃)_(n−1)M_(n)X_(3n+1)  (I);(RNH₃)(R′NH₃)(IC)_(n−1)M_(n)X_(3n+1)  (II);wherein R and R′ independently are a monovalent C₆-C₂₀ hydrocarbyl; ICis an inorganic cation comprising a monovalent metal; M is a metalselected from Pb, Sn, Cu, Ge, Mn, Co, Bi, or Eu; X is a halide ionselected from Cl, Br, or I; and n is an integer equal to or greaterthan 1. In one embodiment, the crystal of the nanoscale metal halideperovskite has a 2D structure. In another embodiment, the crystal of thenanoscale metal halide perovskite has a quasi-2D structure. In yetanother embodiment, the crystal of the nanoscale metal halide perovskitehas a 3D structure.

Also provided herein are methods of forming nanoscale metal halideperovskites. In embodiments, the methods comprise providing a precursorliquid comprising a first polar organic liquid, a metal halide, and atleast two cations selected from the group consisting of [1] a smallcation, [2] RNH₃, and [3] R′NH₃, wherein R and R′ are selectedindependently from a C₆-C₂₀ hydrocarbyl, and the small cation is CH₃NH₃or an inorganic cation comprising a monovalent metal; and contacting theprecursor liquid with a second polar organic liquid to form thenanoscale metal halide perovskite. In one embodiment, the methodsfurther comprise providing a first liquid comprising a metal halide andthe first polar organic liquid; providing a second liquid comprising theat least two cations; and combining the first liquid and the secondliquid to form the precursor liquid.

BRIEF DESCRIPTION OF THE FIGURES

FIG. 1 is a schematic of various crystal structures of severalembodiments of nanoscale metal halide perovskites.

FIG. 2A depicts the absorbance spectra of several embodiments ofnanoscale metal halide perovskites.

FIG. 2B depicts the emission intensity of several embodiments ofnanoscale metal halide perovskites.

FIG. 3 depicts X-ray diffraction data for several embodiments ofnanoscale metal halide perovskites.

FIG. 4 depicts a schematic of various crystal structures of severalembodiments having a quasi-2D structure.

FIG. 5A is a transmission electron microscopy (TEM) image of oneembodiment of a nanoscale metal halide perovskite and its electrondiffraction pattern (inset).

FIG. 5B is a TEM image of one embodiment of a nanoscale metal halideperovskite and its electron diffraction pattern (inset).

FIG. 5C is a TEM image of one embodiment of a nanoscale metal halideperovskite and its electron diffraction pattern (inset).

FIG. 5D is a TEM image of one embodiment of a nanoscale metal halideperovskite and its electron diffraction pattern (inset).

FIG. 5E is a TEM image of one embodiment of a nanoscale metal halideperovskite and its electron diffraction pattern (inset).

FIG. 5F is a TEM image of one embodiment of a nanoscale metal halideperovskite and its electron diffraction pattern (inset).

DETAILED DESCRIPTION

Provided herein are nanoscale metal halide perovskites, such asnanoscale lead (II) bromide perovskites, that can have 2D, quasi-2D, or3D layered structures, and may be prepared by relatively simple methods,including a one-pot synthesis procedure. The methods provided herein maybe performed at room temperature, result in product yields of at least70%, and/or produce metal halide perovskites of high quality. Thenanoscale metal halide perovskites may be color tunable, be stable,and/or have high quantum efficiencies. The nanoscale metal halideperovskites provided herein may have different quantum size confinementto enable color tuning, and the quantum size confinement may becontrolled by the methods provided herein.

In embodiments, the nanoscale metal halide perovskites provided hereincomprise a crystal having a unit cell according to formula (I):(RNH₃)(R′NH₃)(CH₃NH₃)_(n−1)M_(n)X_(3n+1)  (I);wherein R and R′ are selected independently from a monovalent C₆-C₂₀hydrocarbyl; M is a metal selected from Pb, Sn, Cu, Ge, Mn, Co, Bi, orEu; X is a halide ion selected from Cl, Br, or I; and n is an integerequal to or greater than 1. In one embodiment, n represents the numberof inorganic metal halide layers.

In one embodiment of the nanoscale metal halide perovskites of formula(I), M is Pb, X is Br, and the nanoscale metal halide perovskitescomprise a crystal having a unit cell according to formula (IA):(RNH₃)(R′NH₃)(CH₃NH₃)_(n−1)Pb_(n)Br_(3n+1)  (IA).

In one embodiment of the nanoscale metal halide perovskites of formula(I), M is Pb, X is Br, R and R′ are identical, and the nanoscale metalhalide perovskite comprises a crystal having a unit cell according toformula (IB):(RNH₃)₂(CH₃NH₃)_(n−1)Pb_(n)Br_(3n+1)  (IB).

In embodiments, the nanoscale metal halide perovskites provided hereincomprise a crystal having a unit cell according to formula (II):(RNH₃)(R′NH₃)(IC)_(n−1)M_(n)X_(3n+1)  (II);wherein IC is an inorganic cation comprising a monovalent metal; R andR′ are selected independently from a monovalent C₆-C₂₀ hydrocarbyl; M isa metal selected from Pb, Sn, Cu, Ge, Mn, Co, Bi, or Eu; X is a halideion selected from Cl, Br, or I; and n is an integer equal to or greaterthan 1. In one embodiment, n represents the number of inorganic metalhalide layers. In some embodiments, the monovalent metal comprises Cs orRb. In a particular embodiment, the monovalent metal is Cs. In anotherembodiment, the monovalent metal is Rb.

In one embodiment of the nanoscale metal halide perovskites of formula(II), M is Pb, X is Br, and the nanoscale metal halide perovskitescomprise a crystal having a unit cell according to formula (IIA):(RNH₃)(R′NH₃)(IC)_(n−1)Pb_(n)Br_(3n+1)  (IIA).

In one embodiment of the nanoscale metal halide perovskites of formula(IIA), IC is Cs, and the nanoscale metal halide perovskites comprise acrystal having a unit cell according to formula (IIB):(RNH₃)(R′NH₃)(Cs)_(n−1)Pb_(n)Br_(3n+1)  (IIB).

In one embodiment of the nanoscale metal halide perovskites of formula(II), IC is Cs, M is Pb, X is Br, R and R′ are identical, and thenanoscale metal halide perovskite comprises a crystal having a unit cellaccording to formula (IIC):(RNH₃)₂(Cs)_(n−1)Pb_(n)Br_(3n+1)  (IIC).

In the crystals having a unit cell according to any of formulas (I),(IA), (IB), (II), (IIA), (IB), and (IIC), n may be [1]1, therebyimparting the crystals with a 2D structure, [2] 2-9, thereby impartingthe crystal with a quasi-2D structure, or [3] 10 or greater, therebyimparting the crystals with a 3D structure.

In one embodiment, R and R′ are selected independently from a monovalentC₇-C₁₈ hydrocarbyl. In another embodiment, R and R′ are selectedindependently from a monovalent C₇-C₈ hydrocarbyl. In yet anotherembodiment, R and R′ are selected independently from a monovalentC₁₆-C₁₈ hydrocarbyl.

In one embodiment, R and R′ are different monovalent C₆-C₂₀hydrocarbyls. As used herein, the phrase “different monovalent C₆-C₂₀hydrocarbyls” can refer to [1] two hydrocarbyls that include differentnumbers of carbon atoms; [2] two hydrocarbyls that include the samenumber of carbon atoms, but are substituted with the “—NH₃” functionalgroups at a different carbon atom; or [3] two hydrocarbyls that includethe same number of carbon atoms, but are different stereoisomers. Inanother embodiment, R and R′ are identical monovalent C₆-C₂₀hydrocarbyls.

The phrases “C₁-C₂₀ hydrocarbyl,” “C₇-C₁₈ hydrocarbyl,” “C₇-C₈hydrocarbyl,” and the like, as used herein, generally refer toaliphatic, aryl, or arylalkyl groups containing 1 to 20, 7 to 18, or 7to 8 carbon atoms, respectively. Examples of aliphatic groups, in eachinstance, include, but are not limited to, an alkyl group, a cycloalkylgroup, an alkenyl group, a cycloalkenyl group, an alkynyl group, analkadienyl group, a cyclic group, and the like, and includes allsubstituted, unsubstituted, branched, and linear analogs or derivativesthereof, in each instance having 1 to about 20 carbon atoms, 7 to 18carbon atoms, 7 to 8 carbon atoms, etc. Examples of alkyl groupsinclude, but are not limited to, methyl, ethyl, propyl, isopropyl,n-butyl, t-butyl, isobutyl, pentyl, hexyl, isohexyl, heptyl,4,4-dimethylpentyl, octyl, 2,2,4-trimethylpentyl, nonyl, decyl, undecyland dodecyl. Cycloalkyl moieties may be monocyclic or multicyclic, andexamples include cyclopropyl, cyclobutyl, cyclopentyl, cyclohexyl, andadamantyl. Additional examples of alkyl moieties have linear, branchedand/or cyclic portions (e.g., 1-ethyl-4-methyl-cyclohexyl).Representative alkenyl moieties include vinyl, allyl, 1-butenyl,2-butenyl, isobutylenyl, 1-pentenyl, 2-pentenyl, 3-methyl-1-butenyl,2-methyl-2-butenyl, 2,3-dimethyl-2-butenyl, 1-hexenyl, 2-hexenyl,3-hexenyl, 1-heptenyl, 2-heptenyl, 3-heptenyl, 1-octenyl, 2-octenyl,3-octenyl, 1-nonenyl, 2-nonenyl, 3-nonenyl, 1-decenyl, 2-decenyl and3-decenyl. Representative alkynyl moieties include acetylenyl, propynyl,1-butynyl, 2-butynyl, 1-pentynyl, 2-pentynyl, 3-methyl-1-butynyl,4-pentynyl, 1-hexynyl, 2-hexynyl, 5-hexynyl, 1-heptynyl, 2-heptynyl,6-heptynyl, 1-octynyl, 2-octynyl, 7-octynyl, 1-nonynyl, 2-nonynyl,8-nonynyl, 1-decynyl, 2-decynyl and 9-decynyl. Examples of aryl orarylalkyl moieties include, but are not limited to, anthracenyl,azulenyl, biphenyl, fluorenyl, indan, indenyl, naphthyl, phenanthrenyl,phenyl, 1,2,3,4-tetrahydro-naphthalene, tolyl, xylyl, mesityl, benzyl,and the like, including any heteroatom substituted derivative thereof.

Unless otherwise indicated, the term “substituted,” when used todescribe a chemical structure or moiety, refers to a derivative of thatstructure or moiety wherein one or more of its hydrogen atoms issubstituted with a chemical moiety or functional group such as alcohol,alkoxy, alkanoyloxy, alkoxycarbonyl, alkenyl, alkyl (e.g., methyl,ethyl, propyl, t-butyl), alkynyl, alkylcarbonyloxy (—OC(O)alkyl), amide(—C(O)NH-alkyl- or -alkylNHC(O)alkyl), tertiary amine (such asalkylamino, arylamino, arylalkylamino), aryl, aryloxy, azo, carbamoyl(—NHC(O)O— alkyl- or —OC(O)NH-alkyl), carbamyl (e.g., CONH₂, as well asCONH-alkyl, CONH-aryl, and CONH-arylalkyl), carboxyl, carboxylic acid,cyano, ester, ether (e.g., methoxy, ethoxy), halo, haloalkyl (e.g.,—CCl₃, —CF₃, —C(CF₃)₃), heteroalkyl, isocyanate, isothiocyanate,nitrile, nitro, phosphodiester, sulfide, sulfonamido (e.g., SO₂NH₂),sulfone, sulfonyl (including alkylsulfonyl, arylsulfonyl andarylalkylsulfonyl), sulfoxide, thiol (e.g., sulfhydryl, thioether) orurea (—NHCONH-alkyl-).

For example, R and R′ may be selected independently from a monovalentC₇-C₁₈ hydrocarbyl that includes n-octadec-1-yl, n-oct-1-yl, or benzyl.In one embodiment, R is selected from a monovalent n-octadec-1-yl or amonovalent n-oct-1-yl, and R′ is a monovalent benzyl. In anotherembodiment, R and R′ are a monovalent n-octadec-1-yl. In a furtherembodiment, R and R′ are a monovalent n-oct-1-yl. Therefore, in thecrystals having a unit cell according to any of formulas (I), (IA),(IB), (II), (IIA), (IIB), and (IIC), [1] R and R′ may be selectedindependently from a monovalent n-octadec-1-yl, a monovalent n-oct-1-yl,or a monovalent benzyl, [2] R may be selected from a monovalentn-octadec-1-yl or a monovalent n-oct-1-yl, and R′ may be a monovalentbenzyl, [3] R and R′ may be a monovalent n-octadec-1-yl, and [4] R andR′ may be a monovalent n-oct-1-yl.

Structures

The nanoscale metal halide perovskites provided herein generally mayhave a 2D structure, a quasi-2D structure, or a 3D structure.

Not wishing to be bound by any particular theory, it is believed thatthe value of “n” in unit cell formulas provided herein, such as “formula(I)” or “formula (II),” may determine whether a nanoscale metal halideperovskite has a 2D, quasi-2D, or 3D structure. As depictedschematically at FIG. 1, it is believed that at least in certainembodiments wherein M is Pb and X is Br, the nanoscale metal halideperovskites have a 2D structure when n is 1, a quasi-2D structure when nis 2 (see FIG. 1), 3 (see FIG. 1), or 4-9, and a 3D structure when n is10 or greater.

As used herein, the phrases “2D structure” or “2D layered structure”generally refer to a crystal having unit cells of formula (I) or (II)wherein n is 1 (see FIG. 1), and, not wishing to be bound by anyparticular theory, it is believed that the crystals having a “2Dstructure” include a metal halide inorganic layer sandwiched between twoorganic layers.

As used herein, the phrases “3D structure” or “3D layered structure”generally refer to a crystal having unit cells of formula (I) or (II)wherein n is at least 10, for example, 00 (see FIG. 1), and, not wishingto be bound by any particular theory, it is believed that the crystalshaving a “3D structure” include methylammonium metal halides capped withhydrocarbylamines.

As used herein, the phrases “quasi-2D structure” or “quasi-2D layeredstructure” generally refer to a crystal having unit cells of formula (I)or (II) wherein n is 2 (see FIG. 1), 3 (see FIG. 1), or 4-9, and, notwishing to be bound by any particular theory, it is believed that thecrystals having a “quasi-2D structure” include “n” continuous metalhalide layers sandwiched between two organic layers comprisinghydrocarbylammonium ligations.

Not wishing to be bound by any particular theory, it is believed thatsynthetically manipulating a quasi-2D structure of a nanoscale metalhalide perovskite can permit different quantum size confinement effectsto be realized. The different quantum size confinement effects mayenable precise color tuning of emission, for example, from deep blue tobright green. For example, the nanoscale metal halide perovskitesdepicted at FIG. 1 emit deep blue light when n is 1, blue light when nis 2, light blue light when n is 3, and bright green light when n is 00.

In embodiments, the nanoscale metal halide perovskites provided hereinemit light having a wavelength of about 403 nm (deep blue) to about 530nm (bright green).

In embodiments, the nanoscale metal halide perovskites provided hereinhave a PLQE of about 13% to about 45%.

In embodiments, the the nanoscale metal halide perovskites providedherein emit light having a wavelength of about 403 nm (deep blue) toabout 530 nm (bright green), and have a PLQE of about 13% to about 45%.

Methods for Making Nanoscale Perovskites

Methods also are provided for making nanoscale metal halide perovskites.The methods provided herein may permit synthetic control of “n” of theunit cell formulas herein. Not wishing to be bound by any particulartheory, it is believed that controlling the value of “n” may result indifferent quantum size confinement in the nanoscale metal halideperovskites, thereby enabling color tuning. For example, it is believed,at least in certain embodiments, that increasing n of formula (I) or(II) herein from 1 to various integers and to infinity, the emissionred-shifts from deep blue to bright green. This structure-propertyrelationship may permit color tuning, because, at least in certainembodiments, the photophysical properties can correlate to thematerials' composition and structure.

Alternatively or in addition to adjusting the n of formula (I) or (II)herein, it is believed that color tuning of the nanoscale metal halideperovskites provided herein can be realized, at least in someembodiments, by manipulating the organic cations. Not wishing to bebound by any particular theory, it is believed that manipulating theorganic cations can afford 2D, quasi-2D, and/or 3D structures havingdifferent quantum confinement effects.

In embodiments, the methods comprise providing a precursor liquidcomprising a first polar organic liquid, a metal halide, and at leasttwo cations selected from the group consisting of [1] a small cation,[2] RNH₃, and [3] R′NH₃, wherein R and R′ are selected independentlyfrom a monovalent C₆-C₂₀ hydrocarbyl, and the small cation is CH₃NH₃ oran inorganic cation comprising a monovalent metal; and contacting theprecursor liquid with a second polar organic liquid to form thenanoscale metal halide perovskite. The ratio of the at least two cationsmay be manipulated. R and R′ may be identical. In a particularembodiment, the at least two cations consist of RNH₃ and R′NH₃. Themonovalent C₆-C₂₀ hydrocarbyl of R and R′ may be independently selectedfrom n-octadec-1-yl, n-oct-1-yl, or benzyl.

The metal halide may comprise Pb, Sn, Cu, Ge, Mn, Co, Bi, or Eu. In oneembodiment, the metal halide is lead (II) halide. In a particularembodiment, the metal halide is lead (II) bromide.

The organic ammonium cations, i.e., CH₃NH₃, RNH₃, and R′NH₃, may beammonium salts, such as CH₃NH₃ ⁻X⁺, RNH₃ ⁻X⁺, and R′NH₃ ⁻X⁺, wherein Xis a halogen. In one embodiment, the at least two cations are ammoniumsalts prepared by adding a slight excess of HX, wherein X is a halogen,such as bromine, to an amine, such as CH₃NH₂, RNH₂, and R′NH₂. Thisaddition may be performed at about 0° C. and/or in a C₁-C₁₀ alcohol,such as ethanol. The solvents then may be evaporated under vacuum. Theamines may include octadecylamine, octylamine, benzylamine, methylamine,or a combination thereof. Not wishing to be bound by any particulartheory, it is believed that nanoscale lead (II) bromide perovskiteshaving a 2D structure may be prepared by using benzylamine as an amine;and amines having longer organic portions, such as octadecylammoniumbromide, may be used to prepare nanoscale metal halide perovskiteshaving a 3D structure.

The inorganic cation comprising a monovalent metal can be a monovalentmetal halide, such as CsX or RbX, wherein X is a halogen, such as Br. Inone embodiment, the monovalent metal halide is CsBr. In anotherembodiment, the monovalent metal halide is RbBr.

In embodiments, the methods comprise providing a first liquid comprisinga metal halide and the first polar organic liquid; providing a secondliquid comprising the at least two cations; and combining the firstliquid and the second liquid to form the precursor liquid.

The precursor liquid may be transparent. In one embodiment, theprecursor liquid comprises lead (II) bromide and is a transparentprecursor liquid.

The first polar organic liquid of the precursor liquid generally may beany polar organic liquid that does not substantially impact theformation of the nanoscale metal halide perovkites. In one embodiment,the first polar organic liquid is dimethyl formamide (DMF).

In one embodiment, the methods further comprise contacting the precursorliquid with a non-polar organic liquid prior to contacting the precursorliquid with the second polar organic liquid. The non-polar liquid maycomprise hexane, cyclohexane, isomers of hexane, or a combinationthereof. In a particular embodiment, contacting the precursor liquidwith the non-polar organic liquid, such as hexane, comprises injectingthe precursor liquid into the non-polar liquid. The non-polar liquid,such as hexane, may be stirred before, during, and/or after theinjection. The non-polar liquid also may be at room temperature before,during, and/or after the injection.

The methods may also comprise contacting the precursor liquid with asecond polar organic liquid, such as acetone, to form the nanoscalemetal halide perovskite. In one embodiment, contacting the precursorliquid with the second polar organic liquid, such as acetone, results inthe formation of a colloidal liquid. The colloidal liquid may becentrifuged. The first and second polar liquids, the non-polar liquid,and/or any unreacted starting materials may be removed by any meansknown in the art.

The nanoscale metal halide perovskites may be produced at a yield of atleast 50%, at least 65%, at least 70%, at least 75%, at least 80%, atleast 85%, at least 90%, or at least 95%. The yield of nanoscale metalhalide perovskites, unless otherwise noted, refers to the yieldcalculated from the results of thermogravimetric analysis, and is basedon the weight of metal halide in the nanoscale perovskites compared tothe weight of metal halide used in the reaction (starting amount). Theas-prepared nanoscale metal halide perovskites can be re-dispersed intoluene.

EXAMPLES

The present invention is further illustrated by the following examples,which are not to be construed in any way as imposing limitations uponthe scope thereof. On the contrary, it is to be clearly understood thatresort may be had to various other aspects, embodiments, modifications,and equivalents thereof which, after reading the description herein, maysuggest themselves to one of ordinary skill in the art without departingfrom the spirit of the present invention or the scope of the appendedclaims. Thus, other aspects of this invention will be apparent to thoseskilled in the art from consideration of the specification and practiceof the invention disclosed herein.

Unless otherwise noted, the following materials were used in thefollowing Examples. Lead (II) bromide (99.999%), methylamine solution(33 wt. % in absolute ethanol), octylamine (99%), benzylamine (99%),octadecylamine (99%) and hydrobromic acid (48%) were purchased fromSigma-Aldrich. Acetone (99.5%) was purchased from VWR.N,N-Dimethylformamide (99.9%), toluene (99.9%) and hexane (98.5%,mixture of isomers) were purchased from Sigma-Aldrich. All reagents andsolvents were used without further purification unless otherwise stated.Spectroscopic grade solvents were used in the UV-Vis andphotoluminescence spectroscopic measurements.

Example 1—Synthesis of Nanoscale Perovskites

A quasi-2D layered nanoperovskite was made by forming a first liquid bydissolving 0.1 mmol lead(II) bromide (0.10 mmol, 36.7 mg) in 200 μL DMF.

A second liquid was them formed by mixing 33.6 mg octylammonium bromide(0.16 mmol) and 11.2 mg methylammonium bromide (0.10 mmol) in 100 μLDMF.

The first liquid and the second liquid were them combined to form aclear precursor liquid (300 μL DMF in total), which was subsequentlydropped into 2 mL hexanes with vigorously stirring for 5 min at roomtemperature.

The corresponding nanoperovskites were induced by adding 3 mL acetone,followed by centrifugation to remove the unreactive materials in thesupernatant. This process afforded the final products at the yieldsshown at Table 1, which were calculated after drying the nanoperovskitesunder vacuum.

Using the foregoing procedure, a series of nanoscale perovskites weremade with different organic ammonium bromides. The types and amounts ofthe organic ammonium bromides and amount of lead bromide used for eachproduct are summarized at Table 1. The sample names, such as “NP403”,indicate the maximum emission wavelength observed for each sample, i.e.,403 nm for “NP403”.

TABLE 1 Composition of the nanoperovskites of Example 1, according toTGA and ¹H NMR. Starting Calcu- amount/ Molar lated Chemical ProductReagent mmol ratio^(a) ratio^(b) yield^(c) NP403 C₈H₁₇NH₃Br 0.16 0.120.22 76% C₆H₅CH₂NH₃Br 0.24 1.82 1.78 PbBr₂ 0.10 1.00 1.00 NP442C₈H₁₇NH₃Br 0.20 1.46 0.67 74% CH₃NH₃Br 0.05 0.66 0.67 PbBr₂ 0.10 1.001.00 NP461 C₈H₁₇NH₃Br 0.16 0.59 0.40 72% CH₃NH₃Br 0.10 0.81 0.80 PbBr₂0.10 1.00 1.00 NP499 C₈H₁₇NH₃Br 0.07 0.11 0.18 75% CH₃NH₃Br 0.20 1.110.91 PbBr₂ 0.10 1.00 1.00 NP513 C₈H₁₇NH₃Br 0.05 0.07 0.12 76% CH₃NH₃Br0.20 1.12 0.94 PbBr₂ 0.10 1.00 1.00 NP530 C₁₈H₃₇NH₃Br 0.01 0.04 0.06 75%CH₃NH₃Br 0.20 1.18 0.97 PbBr₂ 0.10 1.00 1.00 ^(a)Calculated from the TGAand ¹H NMR results, and based on the mol of PbBr₂; ^(b)Calculated fromthe XRD and AFM results, and based on the chemical formula of(RNH₃)₂(CH₃NH₃)_(n−1)Pb_(n)Br_(3n+1); ^(c)Calculated from the TGAresults, and based on the weight of PbBr₂ in the nanoperovskitescompared to the weight of PbBr₂ used in the reaction (starting amount).

The molar ratios of the organic ligands in the samples of this Examplewere estimated by dissolving the samples in DMSO-d₆ and analyzing the ¹HNMR spectra. The results are summarized at Table 1. The composition ofthe organic (ammonium bromides) and inorganic (lead bromide) moietieswas also confirmed by TGA analysis. Two major weight losses wereobserved for all of the samples at 300° C. and 550° C., which wasbelieved to correspond to the losses of the organic ammonium bromidesand the inorganic lead bromides, respectively.

Based on the results from both NMR and TGA analysis, the molar ratio ofeach component in the samples was calculated (see Table 1). For NP442and NP461, the molar ratios of methylammonium bromide to lead(II)bromide were 0.66 and 0.81, respectively, which were very close to thetheoretical ratios of 2:3 and 4:5 in n=3 and n=5 quasi-2D layeredstructures. However, the calculated amount of octylammonium bromide wasslightly larger than the theoretical value in both cases, which wasbelieved to indicate that the aliphatic ammonium ligands acted not onlyas the building blocks of the perovskite structures, but also assurfactants to form and stabilize the reverse micelles in solutions.

To permit the relatively easy manipulation of the ratios of the organiccations, the ammonium salts were prepared first.

The organic ammonium bromide salts used to prepare the nanoperovskitesof this example were prepared by adding a slight excess of a hydrobromicacid solution (48%) into the corresponding amines, respectively, inethanol at 0° C. The ammonium salts were obtained after removal of thesolvents and starting reagents under vacuum, followed by washing withethyl ether by three times, after which the ammonium bromides were driedand kept in a desiccator for future use.

The as-prepared nanoperovskites of this Example were dispersed intoluene, and resulted in samples ranging from colorless to light greenunder ambient light. Under UV irradiation (λ_(ex)=365 nm), however, thenanoperovskites of this example exhibited a significant color changefrom deep blue to green. Not wishing to be bound by any particulartheory, it was believed that this could be attributed to the quantumconfinement caused by the quasi-2D layered structure having inorganiclayers of different thicknesses.

Example 2—Characterization of Nanoscale Perovskites

To elucidate the composition and structure of the obtained lead(II)bromide nanoperovskites of Example 1, full characterizations withTransmission Electron Microscopy (TEM), X-Ray Diffraction (XRD), AtomicForce Microscopy (AFM), Proton Nuclear Magnetic Resonance (1H NMR), andThermal Gravimetric Analysis (TGA) were carried out.

Nuclear Magnetic Resonance (1H-NMR):

1H NMR spectra were acquired at room temperature on Bruker AVANCE IIINMR Spectrometers with a 500 MHz Bruker magnet. All chemical shifts (6)were reported in ppm relative to tetramethylsilane (TMS).

Thermogravimetry Analysis (TGA):

TGA was carried out using a TA instruments Q50 TGA system. The sampleswere heated from room temperature (˜22° C.) to 800° C. with at a rate of5° C.·min⁻¹, under a nitrogen flux of 100 mL·min⁻¹.

X-Ray Powder Diffraction (XRPD):

The XRD analysis was performed on Panalytical X'PERT Pro Powder X-RayDiffractometer using Copper X-ray tube (standard) radiation at a voltageof 40 kV and 40 mA, and X'Celerator RTMS detector. The diffractionpattern was scanned over the angular range of 5-70 degree (2θ) with astep size of 0.02, at room temperature.

The XRD patterns of the thin film samples of Example 1 were recorded asshown at FIG. 3 and summarized in Table 2, which can be used to quantifythe layered crystalline structures of these NPs.

TABLE 2 XRD analyses including miller index, 2θ degree and latticespaces (d). Sample (h k l) 2θ degree d (Å) NP403 (0 0 2) 5.29 16.67 (0 04) 10.58 8.34 (0 0 6) 15.93 5.54 (0 0 8) 21.26 4.15 (0 0 10) 26.66 3.31(0 0 12) 32.16 2.75 (0 0 14) 37.66 2.35 NP442 (0 0 6) 10.02 8.81 (0 0 8)13.36 6.61 (0 0 10) 16.73 5.27 (0 0 12) 20.13 4.39 (0 0 14) 23.50 3.76(0 0 16) 26.93 3.28 (0 0 18) 30.39 2.91 (0 0 20) 33.85 2.61 NP461 (0 08) 10.92 8.08 (0 0 10) 13.68 6.45 (0 0 12) 16.45 5.37 (0 0 14) 19.224.59 (0 0 16) 22.02 4.01 (0 0 18) 24.87 3.55 (0 0 20) 27.58 3.20 (0 022) 30.42 2.90 (0 0 24) 33.30 2.65 NP499 (0 0 1) 14.88 5.93 (0 0 2)30.08 2.94 NP513 (0 0 1) 14.88 5.93 (0 1 1) 21.13 4.18 (0 0 2) 30.072.94 (0 1 2) 33.71 2.62 NP530 (0 0 1) 14.87 5.94 (0 0 2) 30.04 2.94

The (00l) diffraction peaks were observed in the NP403 thin film withlayered spacing of 33.34 Å, which was believed to indicate the formationof benzylamine-based 2D perovskite products. This value was consistentwith that of previously reported 2D perovskite nanomaterials.

Also, the layered spacing of NP442 was measured to be 52.86 Å, which wasconsistent with an n=3 quasi-2D layered perovskite structure in view ofthe fact that the interlayer spacing of octylamine-based 2D perovskitesis 42.1 Å (42.1 Å+2×5.91 Å) (see N. Kitazawa et al. Thin Solid Films,2006, 500, 133-137; and N. Kitazawa et al. J Lumin, 2009, 129,1036-1041).

The layered spacing of NP461 was measured to be 64.66 Å, which was equalto the layered spacing of NP442 plus two d-spacings of the cubic phaseof 3D lead(II) bromide perovskites (52.86 Å+2×5.91 Å), which wasbelieved to indicate that the n=5 quasi-2D layered perovskite structurewas obtained. The large d-spacings calculated from the diffraction peaksof NP442 and NP461 were believed to confirm the formation of quasi-2Dstructure as shown at FIG. 4. When the number of inorganic layersincreased further (i.e. NP499, NP513 and NP530), the (100) and (200)diffraction peaks from the 3D lead(II) bromide perovskite structureswere observed. Not wishing to be bound by any particular theory, it wasbelieved that the sets of the minor peaks (impurity) might have beenintroduced during the sample preparation of XRD spectra, probably due tothe decomposition or aggregation of the samples.

Transmission Electron Microscopy Images (TEM):

Microstructural characterization was performed using TEM, on a JEOLJEM-ARM200cF at 200 kV. Low intensity illumination and fast acquisitiontime were used during data collection to avoid beam damage. TEM sampleswere prepared by depositing a few drops of the perovskite solution on acarbon film supported copper grid (200 mesh); the samples weresubsequently dried overnight.

FIG. 5A, FIG. 5B, FIG. 5C, FIG. BD, FIG. 5E, and FIG. 5F are TEM imagesof NP403, NP442, NP461, NP499, NP513, and NP530, respectively, withtheir electron diffraction patterns (insets). All of the as-preparedmetal halide perovskites displayed at least substantially rectangularsingle crystalline structures with a lateral dimension size of severalhundred nanometers, except NP403, which had size dimensions on the orderof several micrometers. The lateral size of the nanoscale metal halideperovskites decreased as the amount of methylammonium bromide increased,which was believed to suggest that the speed of the crystal growth inthe lateral direction was faster than in the vertical direction forlayered structures. The inserted electron diffraction patterns showedthe [001] orientation diffraction patterns from the individual metalhalide perovskites, which was believed to suggest a single crystallinestructure for all the nanoscale metal halide perovskites. The d-spacingvalues measured from the electron diffraction patterns were 5.91±0.1 Åand 8.23±0.1 Å of the (100) plane, which corresponded to the cubicphases of the 3D perovskite CH₃NH₃PbBr₃ and tetragonal phases of the 2Dperovskite (C₆H₅CH₂NH₃)₂PbBr₄, respectively.

Atomic Force Microscopy Images (AFM):

AFM measurements were conducted using Bruker Icon. All measurements wereperformed in the standard tapping mode with OTESPA-R3 tips from Bruker.

AFM was employed to further characterize the structure of the nanoscalemetal halide perovskites of Example 1, in particular their thickness.Average thicknesses of 30-120 nm were observed for individual metalhalide perovskites on a silicon wafer, which was believed to suggestthat stacks of quasi-2D layered structures were obtained. The absence ofthe atomically thin perovskites was believed to rule out thethickness-dependent quantum confinement effect in this situation for thenanoscale metal halide perovskites.

Specifically, considering the fact that the thicknesses of a monolayerof NP403, NP442, and NP461 were 3.3 nm, 5.3 nm and 6.5 nm, respectively,from the XRD results, these three metal halide perovskites were found tocontain approximately 9, 9, and 8 stacks of quasi-2D layered structures,respectively.

UV-Visible Measurements:

UV-Vis spectra were conducted at room temperature using a quartzspectrometer cuvette on a Varian Cary 100 Bio UV-Visiblespectrophotometer.

Photoluminescence Steady State Studies:

Steady-state photoluminescence spectra were obtained at room temperatureon a Varian Cary Eclipse Fluorescence spectrophotometer. All the datawere acquired using a 1-cm semi-micro quartz cuvette. The emissionspectra of the perovskites dispersed in toluene were measured under airatmosphere (unless otherwise indicated).

Photoluminescence Quantum Efficiencies:

For photoluminescence quantum efficiency measurement, the samples wereexcited at 360 nm. Absorbance at the excitation wavelength was keptbelow 0.1 to minimize the inner-filter effect. The fluorescence quantumyields were determined by comparing the integrated area of the correctedemission spectrum with that of the reference—quinine bisulfate (ϕ=0.54in 1 N H₂SO₄) (see, S. Fery-Forgues et al. J. Chem. Ed., 1999, 76,1260-1264).

The absorption and emission of the nanoscale metal halide perovskites ofExample 1 in toluene solutions were recorded, as shown at FIG. 2A andFIG. 2B, and summarized in Table 3. The absorption of the nanoscalemetal halide perovskites was red shifted as the amount of methylammoniumbromide used in the reaction was increased.

NP403 showed an absorption peak at 398 nm, which was consistent withpreviously reported 2D perovskites. For NP461 and NP442, it was believedthat the main absorption peaks located at 451 nm and 437 nm,respectively, indicated the formation of quasi-2D layered perovskiteproducts. Also, it was believed that the small, but discernible, peaksbelow the main peaks in both cases might have originated from animpurity (most likely the 2D structure). In the absorption spectrum ofNP530, a peak at 525 nm was observed, which was identical to that oftypical 3D lead(II) bromide perovskite nanomaterials reportedpreviously. The absence of an obvious excitonic peak in NP499 and NP513was believed to indicate a mixture of quasi-2D structures with differentn values.

TABLE 3 Photophysical properties of the quasi-2D layered NPs.^(a)Nanoperovskite λ_(abs) (nm) λ_(em) (nm) FWHM (nm) ϕ (%) NP403 398 403 1113.8% NP442 437 442 16 24.5% NP461 451 461 16 25.8% NP499 490 499 3444.3% NP513 500 513 34 44.0% NP530 525 530 21 20.2% ^(a)λ_(abs) is thewavelength at absorbance maximum; λ_(em), is the wavelength at emissionmaximum; ϕ is the photoluminescence quantum efficiency.

The photoluminescence spectra of as-prepared metal halide perovskites ofExample 1 are shown at FIG. 2B. Ranging from 403 nm to 530 nm, theemissions had low full-width at half-maximum (FWHM) of 11-21 nm (exceptNP499 and NP513), which was believed to suggest that the products wereof high purity. For sample NP475, a main peak at 475 nm appeared alongwith a small shoulder at 460 nm, which was believed to suggest a mixtureof NP461 and NP475. The larger FWHMs of NP499 and NP513 (34 nm) alsowere believed to suggest the formation of a mixture of quasi-2Dstructures. The small Stokes shift of 5-13 nm in all of the samples wasbelieved to imply that the photoluminescence of the nanoscale metalhalide perovskites was generated from a direct exciton recombinationprocess. All samples exhibited reasonably high PLQEs 13.8% (NP403) to44.3% (NP499).

We claim:
 1. A nanoscale metal halide perovskite comprising a crystalhaving a unit cell according to formula (II):(RNH₃)(R′NH₃)(IC)_(n−1)M_(n)X_(3n+1)  (II); wherein IC is an inorganiccation comprising a monovalent metal; R and R′ are selectedindependently from a monovalent C₂-C₂₀ hydrocarbyl; M is a metalselected from Pb, Sn, Cu, Ge, Mn, Co, Bi, or Eu; X is a halide ionselected from Cl, Br, or I; and n is an integer equal to or greater than2.
 2. The nanoscale metal halide perovskite of claim 1, wherein themonovalent metal is Cs or Rb.
 3. The nanoscale metal halide perovskiteof claim 1, wherein n is 2 to 9, and the crystal has a quasi-2Dstructure.
 4. The nanoscale metal halide perovskite of claim 1, whereinn is an integer equal to or greater than 10, and the crystal has a 3Dstructure.
 5. A nanoscale metal halide perovskite comprising a crystalhaving a unit cell according to formula (II):(RNH₃)(R′NH₃)(IC)_(n−1)M_(n)X_(3n+1)  (II); wherein IC is an inorganicmonovalent metal cation; R and R′ are selected independently from amonovalent C₂-C₂₀ hydrocarbyl; M is a metal selected from Pb, Sn, Cu,Ge, Mn, Co, Bi, or Eu; X is a halide ion selected from Cl, Br, or I; nis an integer equal to or greater than 1; and the nanoscale metal halideperovskite has a photoluminescence quantum efficiency (PLQE) of at least44%; wherein when n is 1 the monovalent C₂-C₂₀ hydrocarbyl selected forR is different than the monovalent C₂-C₂₀ hydrocarbyl selected for R′.6. The nanoscale metal halide perovskite of claim 5, wherein theinorganic monovalent metal cation is Cs or Rb.
 7. The nanoscale metalhalide perovskite of claim 5, wherein n is 1, and the crystal has a 2Dstructure.
 8. The nanoscale metal halide perovskite of claim 5, whereinn is 2 to 9, and the crystal has a quasi-2D structure.
 9. The nanoscalemetal halide perovskite of claim 5, wherein n is an integer equal to orgreater than 10, and the crystal has a 3D structure.